Process and composition for the immobilization of radioactive and hazardous wastes in borosilicate glass

ABSTRACT

The present invention provides processes to immobilize radioactive and/or hazardous waste in a borosilicate glass, the waste containing one or more of radionuclides, hazardous elements, hazardous compounds, and/or other compounds. The invention also provides borosilicate glass compositions for use in immobilizing radioactive and/or hazardous waste.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a continuation-in-part of U.S. patent application Ser. No. 11/068,460, filed Feb. 23, 2005, which is herein incorporated by reference in its entirety.

U.S. Provisional Application No. 60/546,202, filed Feb. 23, 2004, and co-pending U.S. patent application Ser. No. 10/606,218 entitled “Processes for Immobilizing Radioactive and Hazardous Wastes” and filed on Jun. 26, 2003, are both incorporated by reference herein in their entireties.

BACKGROUND

1. Field of the Invention

The present invention relates generally to treatment of radioactive and hazardous wastes, and more particularly to processes for immobilizing a waste containing one or more of radionuclides, hazardous elements, hazardous compounds, and other compounds present in the waste.

2. Background of the Invention

The use of radioactive and hazardous materials in the world has led to the accumulation of a significant amount of radioactive and hazardous wastes. There is an international consensus regarding the planned disposal of these wastes by burying them in the ground in deep geological repositories. At the present time, high-level radioactive wastes are being placed in long-term storage awaiting permanent disposal. Once buried, with the passage of time, groundwater and hydrothermal solutions can make contact with the radionuclides, hazardous elements, or hazardous compounds contained in the wastes. As a result, groundwater and hydrothermal solutions can facilitate the leaching of radionuclides, hazardous elements, and hazardous compounds out of the wastes into the biosphere in which plants and animals live. In addition, even without the interference from groundwater and hydrothermal solutions, radionuclides, hazardous elements, or hazardous compounds could possibly diffuse out of the wastes, resulting in contamination of the biosphere. Therefore, improper containment of the wastes can create a significant problem.

There are a number of existing processes that can potentially reduce the leaching and/or diffusion of radioactive and hazardous wastes. The existing processes, however, have various disadvantages. For example, cementation is commonly used to immobilize low-level and intermediate-level radioactive waste. This process is undesirable because a large volume of cement is required to immobilize a small quantity of wastes. Furthermore, cement is highly susceptible to both leaching and diffusion.

The most common method of handling high-level radioactive wastes is vitrification in borosilicate glass. Vitrification is currently being used in a number of countries including France, the United States of America, Korea, Italy, Germany, the United Kingdom, Japan, Belgium, China, and Russia. Conventional vitrification processes, however, are limited in the amount of waste that can be contained, and efforts to increase waste loading capacity of borosilicate glasses or melts have led to high crystallinity, increased rates of leaching, and increased corrosion of the melter, rendering the compositions unsuitable for use in conventional vitrification melters.

Thus, a need exists for improved vitrification processes and borosilicate glass compositions that achieve higher waste loading without the above-mentioned disadvantages on use of the processes and compositions with conventional vitrification melters.

BRIEF SUMMARY OF THE INVENTION

The present invention provides a process for immobilizing radioactive and/or hazardous waste in a borosilicate glass, and compositions for use in the processes. In one aspect of the present invention, a process is provided for immobilizing waste comprising combining the waste with glass-forming components and fluorine in particular proportions, melting the mixture to form a glass with integrated waste with properties suitable for waste vitrification melters, pouring the melted glass with integrated waste into a receptive canister, and solidifying the melted glass with integrated waste by cooling to form a highly polymerized glass, preferably peraluminous, and a glass whose components fall within a designated compositional range.

In another aspect of the present invention, a process is provided for immobilizing waste comprising combining the waste with glass-forming components and fluorine in particular proportions, melting the mixture at a temperature of up to about 1200° C., to form a low viscosity melted glass having a viscosity of about 2 to about 10 Pascal second, with properties suitable for waste vitrification melters, pouring the melted glass with integrated waste into a receptive canister, and solidifying the melted glass with integrated waste by cooling to form a highly polymerized glass, preferably peraluminous, and a glass whose components fall within a designated compositional range.

In a further aspect of the present invention, a process is provided for the immobilization of radioactive and/or hazardous waste in a borosilicate glass. In the process, highly polymerized glass (glass with low numbers of non-bridging oxygen atoms (NBO)) is formed, and used as an immobilizing matrix for radioactive and hazardous waste. The process involves melting together glass-forming and waste components consisting essentially of three groups of compounds: (R₂O+RO), R₂O₃, and (RO₂+R₂O₅), in a ratio of about (1-1.3):(1-1.4):(1.2-4.2), where the final product must also include fluorine in an amount ranging between about 1 and about 3 weight percent. In a preferred embodiment, the ratio between (R₂O+RO) and R₂O₃ is less than or equal to 1.

In yet another aspect of the present invention, a glass composition is provided for the immobilization of radioactive and/or hazardous waste. The glass is a highly polymerized glass consisting essentially of three groups of compounds (R₂O+RO), R₂O₃, and (RO₂+R₂O₅), present in a ratio of about (1-1.3):(1-1.4):(1.2-4.2), where SiO₂ is present in an amount greater than 30 weight percent, B₂O₃ is present in an amount between 8.7 and 15.3 weight percent, Al₂O₃ is present in an amount between 7 and 15.1 weight percent, CaO is present in an amount between 0.2 and 2.3 weight percent, and further where fluorine is present in an amount ranging between about 1 and about 3 weight percent.

The glass formed by these processes, and according to these compositions, incorporates a substantially higher percentage of waste than previously practiced, while at the same time satisfying both the processing requirements and waste form acceptance criteria for glasses produced in waste vitrification melters. Additional advantages and features of the present invention will be apparent from the following drawings, detailed description and examples which illustrate preferred embodiments of the invention.

DETAILED DESCRIPTION OF THE INVENTION

Reference will now be made in detail to the presently preferred embodiments of the invention, which, together with the following examples, serve to explain the principles of the invention. These embodiments are described in sufficient detail to enable those skilled in the art to practice the invention, and it is to be understood that other embodiments may be utilized, and that structural, chemical, and physical changes may be made without departing from the spirit and scope of the present invention.

DEFINITIONS

The term “waste” includes waste materials, such as fission products, which contain radionuclides, hazardous elements, radioactive compounds, hazardous compounds, and/or other components present in the waste. Waste mixtures can include, for example, the following elements and their compounds: Fe, Na, P, Cr, Al, Mn, Ni, Na, Zr, K, Cs, Ru, Sr, Ba, Tc, Rh, Mg, I, lanthanides, actinides (for example, Th, U, Pu, Np, Am, Cm, and Ce), and their compounds, and other components of radioactive and hazardous waste. The waste may also include noble metals and volatile components such as H₂O and/or CO₂. Not all of these elements and their compounds, if separated, are hazardous.

The term “radionuclide” includes any nuclide that emits radiation, including one or more of alpha, beta, and gamma emissions. The term “nuclide” includes an atomic species in which all atoms have the same atomic number and mass number. However, processes in which mixtures of different radionuclides are immobilized are specifically included within the scope of the present invention. Examples of radionuclides are Sr and Cs, and actinides and lanthanides, such as thorium and uranium.

The term “radioactive waste” includes three levels of radioactive wastes classified as follows:

-   -   1. “Low-level radioactive wastes” are generated primarily from         hospitals, laboratories, and the industrial sector. Low-level         radioactive wastes are also generated from constituents that         removed from high-level radioactive wastes. Low-level         radioactive wastes represent about 90% by volume but only about         one percent by radioactivity of all radioactive wastes in the         world.     -   2. “Intermediate-level radioactive wastes” comprise resins,         chemical sludge, and nuclear reactor components.         Intermediate-level radioactive wastes represent about seven         percent by volume and about four percent by radioactivity of all         radioactive wastes in the world.     -   3. “High-level radioactive wastes” comprise spent nuclear         reactor fuel (spent fuel) and other high-level radioactive         wastes generated principally from reprocessing the spent fuel         and from nuclear weapons development. High-level radioactive         wastes represent only about three percent by volume but about         95% by radioactivity of all radioactive wastes in the world.

The term “element” used in the context of radioactive or hazardous elements includes an atomic element of the periodic table. The term “compound” used in the context of hazardous or radioactive compounds includes a substance composed of two or more elements.

The term “hazardous wastes” is defined in the EPA Environmental Glossary as any waste or combination of wastes which pose a substantial present or potential hazard to human health or living organisms because such wastes are non-degradable or persistent in nature or because they can be biologically magnified, or because they can be lethal, or because they may otherwise cause or tend to cause detrimental cumulative effects.

Because many of the compounds of waste mixtures are converted to oxides in a vitrification process, the mixtures are commonly referred to in terms of their “waste oxides” content. The term “waste oxide loading”, “loading of waste oxides”, “waste loading”, or “loading of waste” refers to the weight percentage of the waste mixture (once it is thermally converted to oxides in a vitrification process and which can include non-hazardous components) in the final product of a waste immobilizing process.

As used herein, a “highly polymerized glass” is a glass that has low numbers of non-bridging oxygen (NBO) atoms; a “peraluminous” glass is a glass containing more R₂O₃ than (R₂O+RO); a “peralkaline” glass is a glass containing more (R₂O+RO) than R₂O₃; “Network forming components” are tetrahydrally coordinated cations that are components of R₂O₃ and (RO₂+R₂O₅); “Network modifying components” are highly coordinated cations that are components of RO and R₂O. As used herein, the abbreviation “wt %” means weight percent.

DESCRIPTION

Glasses that have low numbers of NBO (highly polymerized glass) are more chemically durable and less likely to crystallize than glasses with more NBO (low polymerized glass). Examples of fully polymerized glass (100% polymerized with no NBO present in the glass) are feldspar glass compositions, plagioclase glass compositions, and pure silica glass compositions. Examples of highly polymerized glass (˜90% or greater polymerization with low numbers of NBO) are natural glasses such as obsidian. Fully or highly polymerized glass has a greater capacity to incorporate additional components while maintaining the chemical durability of the glass than do low or depolymerized glass. This is due to the fact that highly polymerized structures have many more bonds to be broken than do low polymerized structures. In addition, in low polymerized glasses, alkali and alkaline ions are bonded with NBO and therefore are more mobile and reactive. They more easily exchange with hydronium ions in water and also cause more crystallization than when they are more tightly bonded in glasses with few NBO.

Highly polymerized melts or glasses have extremely high viscosities and are therefore not suitable for vitrification in conventional waste vitrification melters, which process in the temperature range of 1150-1200° C. In the case of albite, for example, when melted to 1200° C., the melt has a viscosity of approximately 10⁵ Pascal second. This is due to the fact that the melt is being heated only about 87° C. above its melting point (1113° C.). In the case of plagioclase glass compositions or feldspar glass compositions, for example, when melted to 1150° C., the melt has a viscosity of approximately 10⁴ Pascal second. This viscosity is estimated using E. Persikov's model based on the Carron principle. The same viscosity is calculated using the Y. Botting a and D. F. Weill model, as described in The Viscosity of Magmatic Silicate Liquids; a Model for Calculation, Amer. J. Sci., 272, pp. 438-475.

There are several ways to reduce viscosity in highly polymerized glass. For example, the addition of alkalis breaks Si—O bonds and creates NBOs, thereby reducing viscosity. Another method for reducing viscosity is by adding glass-forming components or fluxes, e.g. B₂O₃, which reduce the melting temperature of the material. The most effective flux is fluorine. In contrast to other fluxes, even the first 2 wt % of fluorine in the glass may decrease viscosity several times more than that provided by the same amount of alkali(s). Although this characteristic of fluorine is known, the deliberate use of fluorine has been purposefully avoided in waste vitrification glass formulations due to its chemical reactivity, which may cause corrosion in waste vitrification melters or other waste treatment unit operations. Additionally, higher fluorine concentrations can lead to phase separation in some glass forming systems.

Fluorine may either be originally present in the waste or may be added anytime later to the waste or may be partially found as an original component of the waste and partially as a later additive to the waste. However, a low concentration of fluorine (up to about 3 wt %) may dramatically reduce viscosity while not having any significant adverse effect on the melter, or other waste treatment process components. The viscosity of the glass compositions developed according to this invention is relatively low (approximately 2 to 10 Pascal second at glass processing temperatures).

Although fully or highly polymerized glass has a greater capacity to incorporate additional components while maintaining the chemical durability of the glass than does low or depolymerized glass, highly polymerized glasses inherently have high viscosities that render them unsuitable for use in conventional vitrification melters. The advantage of our invention is two-fold: firstly, it enables higher waste loadings than have been previously achieved using borosilicate glass in existing vitrification systems while also satisfying processing and product quality requirements for waste vitrification (i.e., viscosity, electrical resistivity, crystallization, and chemical durability. For example, the borosilicate glass compositions of this invention have specific electrical resistivity ranging between about 1.4 Ωcm to about 10 Ωcm at about 1150 degrees Celsius, that is acceptable for processing in vitrification melters, and meet the leaching requirements of less than about 1.19 grams per square meter per day for boron, less than about 0.69 grams per square meter per day for lithium, and less than about 0.95 grams per square meter per day for sodium, for acceptance in U.S. high-level waste repositories. See, for example, U.S. DOE/RW Waste Acceptance System Requirements Document (WASRD), and the Tanks Focus Area High-Level Waste Melter Study Report, prepared in July 2001 for the U.S. Department of Energy by Pacific Northwest National Laboratory, Section 3.0, for processing and product quality requirements in the U.S. See, for example, DOE-EM-0177, High-Level Waste Borosilicate Glass: A Compendium of Corrosion Characteristics, U.S DOE, 1994, for product requirements outside the U.S. See, for example, Radioactive Waste Forms for the Future, eds. W. Lutze and R. C. Ewing, Elsevier Science, 1988, Chapter 1, for processing and product requirements outside the U.S.) Secondly, it enables the achievement of these high waste loadings according to an algorithm, without necessitating empirical trial and error. Both of these advantages render this invention commercially valuable.

The degree of polymerization of a glass is determined by the molar ratio between (a) the sum of monovalent cation oxides (R₂₀) and divalent cation oxides (RO) which are network modifying components, (b) trivalent cation oxides (R₂O₃) which are network forming components, and (c) the sum of tetravalent cation oxides (RO₂) and pentavalent cation oxides (R₂O₅), which are also network forming components. Examples of monovalent cation oxides are Li₂O, Na₂O and K₂O. Examples of divalent cation oxides are CaO, MgO and SrO. Examples of trivalent cation oxides are Al₂O₃ and B₂O₃. Examples of tetravalent cation oxides are SiO₂ and ZrO₂, and MnO₂. Although manganese is found as MnO in the waste compositions presented in the examples, it can be present in various redox states, and therefore, for the purpose of subsequent calculations we assign Mn to the “RO₂” group. An example of a pentavalent cation oxide is P₂O₅. A shorthand manner of depicting or referring to this molar ratio used herein is (R₂O+RO):R₂O₃:(RO₂+R₂O₅). As used herein, “R₂O” refers to a monovalent cation oxide, “RO” refers to a divalent cation oxide, “R₂O₃” refers to a trivalent cation oxide, “RO₂” refers to a tetravalent cation oxide, and “R₂O₅” refers to a pentavalent cation oxide.”

The closer a glass' molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) is to that of a fully polymerized glass such as a feldspathic composition (1:1:6) or a plagioclase composition (between 1:1:6 and 1:1:2), or to a highly polymerized natural glass such as obsidian (1:1:6), the higher the polymerization of the glass. In contrast, the closer a glass' molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) is to that of a low polymerized glass such as a glaucophane composition (5:2:8), the lower the polymerization of the glass. In fact, the critical determinant responsible for a fully or highly polymerized glass is the (R₂O+RO):R₂O₃ part of the ratio, which should be 1:1. It is preferable that the molar part of (R₂O+RO) is equal to or less than the molar part of R₂O₃, because this results in a peraluminous glass. Peraluminous glasses are generally more stable than peralkaline glasses, and therefore peraluminous glasses enable higher waste loadings than peralkaline glasses.

The degree of polymerization of a glass determined by the molar ratio (R₂O+RO):R₂O₃:(RO₂+R₂O₅) may be numerically calculated using the Carron equation (Carron, J. P. (1969) Vue d'ensemble sur la rheologie des magmas silicates naturels, Bul. Soc. Franc. Miner. Cristallogr., 92, 435-446). The Carron equation is as follows:

K=NBO/T*100=[2(O−2T)/T]*100

wherein “K” is the degree of polymerization; “NBO” stands for the “Non-Bridging Oxygen” in the melt; “T” is the total number of network forming gram-ions (such as Al³⁺, Fe³⁺, B³⁺, Si⁴⁺, Zr⁴⁺, P⁵, etc.) that are tetrahedrally coordinated with respect to oxygen and are members of the anionic part of the melt structure; and “O” is the total number of oxygen gram-ions in the melt.

Natural glasses have different degrees of polymerization. Examples include: silica glass—full polymerization (K=0); obsidian—high polymerization (K ranges between >0 and ˜15); andesitic glass—moderate polymerization (K ranges between ˜15 and ˜40); and basaltic glass—low polymerization (K ranges between 40 and ˜70). E. S. Persikov, The Viscosity of Magmatic Liquids, Physical Chemistry of Magmas (Springer-Verlag, 1991), ed. L. L. Perchuk and I. Kushiro, 9, 1-40). For depolymerized glass, K is greater than ˜70. A fully polymerized glass such as the albite composition NaAlSi₃O₈ has a K of 0, as determined by the calculation K=[2(8−2*4)/4]*100=0. A low polymerized glass such as the glaucophane composition Na₂Mg₃Al₂(Si₈O₂₂)(OH)₂ has a K of 40, as determined by the calculation K=[2(22−2*10)/10]*100=40.

A highly polymerized glass may be produced in various ways. For example, one can melt natural or synthetic silicates (such as feldspar or plagioclase), or highly polymerized natural glasses (such as obsidian). Or, for example, glass-forming oxides, or chemical precursors of these oxides (such as quartz, borax, lithium nitrates, etc.) in the correct molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) also produce highly polymerized glass.

In fact, as mentioned above, the critical determinant responsible for a fully or highly polymerized glass is the (R₂O+RO):R₂O₃ part of the ratio, which should be ˜1:1. It is preferable that the molar part of (R₂O+RO) is equal to or less than the molar part of R₂O₃, because this results in a peraluminous glass. Peraluminous glasses are generally more stable than peralkaline glasses, and therefore peraluminous glasses enable higher waste loadings than peralkaline glasses. However, even peralkaline glasses having the (R₂O+RO):R₂O₃ part of the ratio ranging up to 1.3:1 mole parts, will still be highly polymerized, as defined by the Carron equation: K=NBO/T*100. For example, 1.3(R₂O+RO): 1(R₂O₃):2(RO₂) has a K=15, as determined by the calculation K=[2(8.3−8)/4]*100=15.

According to the invention, glass formed to immobilize waste should have physical-chemical and structural properties that are as close as possible to those of highly polymerized glass, e.g., a calculated degree of polymerization (K) of less than about 15, and preferably less than about 7. For example, borosilicate glass is used as a matrix for various waste constituents representative of the high-level radioactive waste found at the Hanford Waste Treatment Plant in Richland, Wash. State. Borosilicate glass is the currently accepted immobilization matrix for the future Hanford Waste Treatment Plant.

To test the invention, waste stimulant compositions were used that were similar to those used by Pacific Northwest National Laboratory (PNNL) and Savannah River Site (SRS) in their models of three different Hanford tank sludges: AZ-101, AZ-102 and C-104, as described in Examples 3, 4, and 2, respectively. According to the invention, the molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) for the borosilicate glass incorporating these three waste simulants are as follows: AZ-101˜1:1.2:4.5; AZ-102˜1:1.2:4.2; and C-104˜1:1.05:2.3. These ratios are close to the (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratio of a fully polymerized plagioclase glass composition. Using the Carron equation, the calculated K ranges of these three glass compositions are between 3.0 and 6.5, which is within the K range of highly polymerized glass.

Prior art borosilicate glasses incorporating these same three Hanford waste simulants had calculated K ranges within the range of moderately to low polymerized glass. For example, the borosilicate glass developed for the Hanford Waste Treatment Plant tested by SRS (E. K. Hansen et. al., Mixing Envelope D Sludge with LAW Intermediate Products with and without Glass Formers, May 2001, Table B-41, p. 115 and Table B-42, p. 117) was used to incorporate AZ-101 and AZ-102 waste simulants, and had (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratios of approximately 2:1:5.7 (AZ-101) and 3.2:1:6.2 (AZ-102). The borosilicate glass formed by PNNL (G. L. Smith et al., Vitrification and Product Testing of C-104 and AZ-102 Pretreated Sludge Mixed with Flowsheet Quantities of Secondary Wastes, February 2001, Table 3.6, pp. 3.10-3.11, and Table 3.9, pp. 3.12-3.13) was used to incorporate C-104 waste simulant, and had an (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratio of approximately 2.5:1:5.8. These SRS and PNNL glass ratios are far from the ratio of fully or highly polymerized glass compositions. Using the Carron equation, the calculated K ranges of these three glass compositions are between 22.5 and 53.6, which is within the K range of moderately to low polymerized glass.

Using the concept of this invention, a 40.8 wt % waste loading was successfully reached using a Hanford C-106 waste simulant (a simulant with a high concentration of iron) as described in Example 1. The 40.8 wt % waste loading that was reached is in contrast to the 25 wt % waste loading currently expected for the Hanford Waste Treatment Plant. The (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratio for the glass of Example 1 is about 1.1:1.17:2, which is the ratio for highly polymerized glass. This glass satisfied all properties required for vitrification in an LCFM melter. The glass composition of Example 1 is suitable to immobilize waste compositions with high amounts of alumina, soda, silica, manganese and iron (high amounts meaning that the total concentration of these components equal more than about 60 to about 70 wt % of the sludge), while at the same time attaining high waste loadings.

Extensive laboratory scale tests have been conducted with high-level waste (HLW) simulants from Hanford and Savannah River. As seen in Table 1 below, experiments were conducted using Hanford batch simulants representative of over 94 volume percent of the Hanford HLW, taken from the Tanks Focus Area High-Level Waste Melter Study Report, Appendix C—Compositions of 89 Waste Batches in Mass Percent of Oxides and Summary Cluster Compositions. In the experiments, which are described in Examples 5-16, borosilicate glass was produced with waste loadings ranging between 40 and 55 weight percent (up to 15 wt % greater than the maximum expected waste loadings for these wastes). In the experiment described in Example 17, borosilicate glass was produced with a waste loading of 40 weight percent for a Savannah River waste.

In Example 5, Batch 69 was immobilized in borosilicate glass with a 43 wt % waste loading. The main component in Batch 69 is Na₂O (23.36 wt %). In the final glass, the concentration of Na₂O is 10.04 wt %. This Na₂O concentration divided by the concentration of Na₂O in the waste equals 0.43, which means that the estimated waste loading for this waste is 43 wt %.

TABLE 1 Comparison Between DOE's Maximum Expected Waste Loadings For Hanford HLW Using Vitrification,* And GeoMatrix's Laboratory Test Results DOE's Maximum GeoMatrix Test Results Representative Mass per Cluster of Principal Expected Waste Loading Achieved Crystallinity at Crystallinity Batch Hanford Hanford HLW to be Components of HLW Using Vitrification** Waste 1150° C. after 3 days at Number HLW Cluster Treated (Tons) in each Cluster (wt %) Loading (wt %) (vol %) 950° C. (vol %) 69 1 2,349 Al, Na, Si 35 43 0   0.5 56 2 1,749 Bi, P 40 55 0   0.2 35 3 1,647 Al, Zr 35 40 <0.3   2*** 46 4 1,395 Na, Al, U 40 45 0.2 <1 53 5 1,384 Na, Al, Bi 40 50 0 <0.5 62 5 ″ ″ 40 40 0 <1 87 6 947 Na, Al 40 50 ~0.3 <0.5 34 7 678 Na, Al 35 50 0 <0.1 32 7 ″ ″ 35 50 0 <1 20 9 426 Zr 35 40 <0.3   2*** 4 11 216 Ag, Fe 50 40 0 <1 30 14 150 Cr, Na 35 40 0 <1 Total 11,679 out of 12,385 tons of HLW at Hanford (94%) *Information taken from TFA HLW Melter Study Report (July 2001), Appendix C and E. **Maximum Expected Waste Loadings have not yet been reached. Typical waste loadings to date using current Hanford HLW simulants are around 25 wt %. ***Average crystal size <10 um.

In Example 6, Batch 56 was immobilized in borosilicate glass with a 55 wt % waste loading. Na₂O is also the main component of Batch 56 (18.57 wt %). In the final glass, the concentration of Na₂O is 10.2135 wt %. This Na₂O concentration divided by the concentration of Na₂O in the waste equals 0.55, which means that the waste loading for this waste is 55 wt %. Batch 56 has an (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratio of approximately 1:1.14:3.9.

In Example 7, Batch 35 was immobilized in borosilicate glass with a 40 wt % waste loading. Na₂O and Al₂O₃ are the main components of Batch 35 (24.87 wt % Na₂O and 27.66 wt % Al₂O₃). In the final glass, the concentration of Na₂O is 9.948 wt % and the concentration of Al₂O₃ is 11.064 wt %. These Na₂O and Al₂O₃ concentrations divided by the Na₂O and Al₂O₃ concentrations in the waste equals 0.40, which means that the waste loading for this waste is 40 wt %. Batch 35 has an (R₂O+RO):R₂O₃:(RO₂+R₂O₅) molar ratio of approximately 1:1.18:2.

The waste loadings of the glasses of the remaining examples (Examples 8-17) can be calculated in the same manner.

As noted above, highly polymerized structures may incorporate more ions than low polymerized structures, without subsequent crystallization. Some waste components are incorporated in the glass. Non-incorporated waste components and extra network forming components apparently form other structural units that interact with the fully or highly polymerized structural units. It is assumed that additional structural units are formed during this process, since higher waste loadings are attained than with other glass compositions, without subsequent crystallization. Irrespective of which components of the waste are incorporated in the highly polymerized structures and which form other structural units, according to this invention, the bulk ratio between (R₂O+RO):R₂O₃:(RO₂+R₂O₅) which determines highly polymerized glass, is maintained.

As a result of experimentation, we have determined that the enhanced waste loading characteristics are achieved using the methodology described herein when the glass consists essentially of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) compounds present in a molar ratio of about (1-1.3):(1-1.4):(1.2-4.2), and where SiO₂ is present in an amount greater than 30 weight percent, B₂O₃ is present in an amount between 8.7 and 15.3 weight percent, Al₂O₃ is present in an amount between 7 and 15.1 weight percent, CaO is present in an amount between 0.2 and 2.3 weight percent, and further where fluorine is present in an amount ranging between about 1 and about 3 weight percent. In a preferred embodiment, fluorine is present in an amount between about 1.2 and about 2.5 weight percent.

As is evident from the use of the term “consists essentially” with respect to the compounds present in the glass composition of the present invention, other compounds or substances may be present in the glass. These other compounds or substances, however, must not be present in such an amount that they interfere with the two advantageous characteristics of this glass provided by the described compositions, i.e., its high polymerization and relatively low viscosity. Generally, keeping other compounds or substances to about 10 weight percent or less of the overall glass composition will maintain these advantageous characteristics, although one skilled in the art will understand the full extent of variation possible, and may calculate such variation according to the teachings of the present invention.

Application of the teachings of the present invention to a specific problem or environment is within the capabilities of one having ordinary skill in the art in light of the teachings contained herein. Examples of the products and processes of the present invention appear in the following examples.

Example 1 Vitrifying Hanford C-106 High-Level Waste (HLW) Simulant with 40.8 Weight Percent Waste Loading

1. The C-106 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40.8 weight percent waste loading.

B C D E A Waste 40.8% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 12.77 5.208883 1.791117 7 B₂O₃ 0.49 0.199871 8.500129 8.7 CaO 1.09 0.444611 0 0.4446 Cl 0.39 0.159081 0 0 Cr₂O₃ 0.28 0.114212 0 0.1142 Cs₂O 0.18 0.073422 0 0.0734 Cu₂O 0.16 0.065264 0 0.06526 F 0.39 0.159081 0 0 Fe₂O₃ 45.35 18.49827 0 18.5 I 0.87 0.354873 0 0.3548 K₂O 0.49 0.199871 8.500129 8.7 La₂O₃ 4.21 1.717259 0 1.7172 Li₂O 1.09 0.444611 0 0.4446 MgO 14.41 5.877839 0 5.8778 MnO 2.11 0.860669 12.13933 13 Na₂O 0.54 0.220266 0 0.2203 Nd₂O₃ 0.62 0.252898 0 0.2528 NiO 0.34 0.138686 0.861314 1 P₂O₅ 0.52 0.212108 0 0.2121 PbO 7.35 2.998065 31.00194 34 Sb₂O₃ 3.31 1.350149 0 1.3501 SeO₂ 0.51 0.208029 0.791971 1 SiO₂ 0.25 0.101975 0 0.1019 SrO₂ 0.97 0.395663 0.604337 1 TiO₂ 0 0 2 2 ZnO 0 0 3.8 3.8 ZrO₂ 12.77 5.208883 1.791117 7

2. Glass-forming components according to the amounts in Column D were added to the C-106 waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the C-106 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1.1:1.17:2.

3. The mixture of step 1 and step 2 was stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results of six tests demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.     -   (c) Viscosity: Ranges from 3.04 Pascal second at 1200° C. to         69.8 Pascal second at 950° C.     -   (d) Specific electrical resistivity: Ranges from 6.14 Ωcm at         1200° C. to 16.29 Ωcm at 950° C.     -   (e) Product Consistency Test (PCT) results (g/m²/d):         Li—2.34×10⁻²; Na—1.78×10⁻²; B—1.04×10⁻²; Al—8.57×10⁻³;         Si—4.94×10⁻³.     -   (f) Toxicity Characteristic Leaching Procedure (TCLP) results         (mg/L): Ni—0.18; Sb—0.10; As—0.019; Cr—0.05; Se—0.10; Zn—0.17.

Example 2

Vitrifying Hanford C-104 High-Level Waste (HLW) Simulant with 45 Weight Percent Waste Loading

1. The C-104 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 45 weight percent waste loading.

B C D E A Waste 45% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 8.723 3.92535 5.1432 9.06855 B₂O₃ 0.021 0.00945 9.25555 9.265 CaO 1.505 0.67725 0 0.67725 CdO 0.24 0.108 0 0.108 Ce₂O₃ 0.275 0.12375 0 0.12375 Cl 0 0 0.0045 0.0045 Cr₂O₃ 0.359 0.16155 0 0.16155 Cs₂O 0.027 0.01215 0 0.01215 Cu₂O 0.073 0.03285 0.00315 0.036 Fe₂O₃ 16.013 7.20585 1.2965 8.50235 F 0 0 1.243 1.243 K₂O 0.076 0.0342 0 0.0342 La₂O₃ 0.43 0.1935 0 0.1935 Li₂O 0 0 1.243 1.243 MgO 0.222 0.0999 1.7751 1.875 MnO 3.195 1.43775 0.48825 1.926 Na₂O 9.925 4.46625 2.96875 7.435 Nd₂O₃ 0.082 0.0369 0.0621 0.099 NiO 0.907 0.40815 0.15885 0.567 P₂O₅ 1.237 0.55665 0 0.55665 PbO 0.4 0.18 0 0.18 Sb₂O₃ 0 0 0 0 SeO₂ 0 0 0 0 SiO₂ 0.906 0.4077 35.7643 36.172 SrO₂ 0.28 0.126 0 0.126 TiO₂ 0.063 0.02835 0 0.02835 ZnO 0.128 0.0576 0 0.0576 ZrO₂ 19.075 8.58375 2.86825 11.452

2. Glass-forming components according to the amounts in Column D were added to the C-104 waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the C-104 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.05:2.3. Zeolite (a natural silicate) was added as a source of part of the glass-forming components.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results of six tests demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: <1 vol % crystals         (zircon) were found.     -   (b) Crystallinity after 3 days at 950° C.: <2 vol % crystals         (zircon) were found.     -   (c) Viscosity: Ranges from 4.10 Pascal second at 1200° C. to         91.0 Pascal second at 950° C.     -   (d) Specific electrical resistivity: Ranges from 3.39 Ωcm at         1200° C. to 9.10 cm at 95° C.     -   (e) PCT results (g/m²/d): Li—7.9×10⁻⁴; Na—5.3×10⁻²; B—5.7×10⁻³;         Si—6.1×10⁻³.     -   (f) TCLP results (mg/L): Ni—0.033; Cr—0.011; Zn—0.19; Pb—0.077.

Example 3

Vitrifying Hanford AZ-101 High-Level Waste (HLW) Simulant with 45 Weight Percent Waste Loading

1. The waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 45 weight percent waste loading.

B C D E A Waste 45% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Ag₂O 0.26 0.117 0 0.117 Al₂O₃ 11.63 5.2335 3.7665 9 B₂O₃ 0 0 11 11 BaO 0.25 0.1125 0 0.1125 CaO 1.34 0.603 0.597 1.2 CdO 2.71 1.2195 0 1.2195 CeO₂ 0.37 0.1665 0 0.1665 CoO 0.39 0.1755 0 0.1755 Cr₂O₃ 0.35 0.1575 0 0.1575 CuO 0.13 0.0585 0 0.0585 F 0 0 2 2 Fe₂O₃ 43.31 19.4895 0.2805 19.77 K₂O 1.23 0.5535 0 0.5535 La₂O₃ 1.44 0.648 0 0.648 Li₂O 0 0 3.5 3.5 MgO 0.28 0.126 0 0.126 MnO 0.91 0.4095 8.5905 9 Na₂O 0.02 0.009 0 0.009 Nd₂O₃ 0.95 0.4275 0 0.4275 NiO 2.37 1.0665 0 1.0665 P₂O₅ 2.54 1.143 0 1.143 PbO 0.37 0.1665 0 0.1665 SiO₂ 3.2 1.44 30.56 32 SrO 0.19 0.0855 0 0.0855 TiO₂ 0.05 0.0225 0 0.0225 ZnO 0.11 0.0495 0 0.0495 ZrO₂ 13.69 6.1605 0 6.1605

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the AZ-101 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range (−1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.2:4.5. Zeolite (a natural silicate) was added as a source of part of the glass-forming components.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results of six tests demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found     -   (c) Viscosity: Ranges from 2.5 Pascal second at 1200° C. to 46.5         Pascal second at 950° C.     -   (d) Specific electrical resistivity: Ranges from 2.91 Ωcm at         1200° C. to 8.65 Ωcm at 950° C.     -   (e) PCT results (g/m²/d): Li—8.0×10⁻⁴; Na—1.3×10⁻³; B—4.55×10⁻³;         Si—8.0×10⁻².     -   (f) TCLP results (mg/L): Ni—0.052; Cr—0.05; Pb—1.1; Ba—3.0;         Ag—0.32; Cd—1.1.

Example 4

Vitrifying Hanford AZ-102 High-Level Waste (HLW) Simulant with 45 Weight Percent Waste Loading

1. The waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 45 weight percent waste loading

B C D E A Waste 45% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 26.28 11.826 2.964 14.7901 B₂O₃ 0 0 8.72 8.72 CaO 0.18 0.081 0.949 1.03 CdO 4.77 2.1465 0 2.1465 Cs₂O 0 0 0.0945 0.0945 F 0 0 1.225 1.225 Fe₂O₃ 40.99 18.4455 1.3456 19.7911 I 0.42 0.189 0 0.189 K₂O 0 0 1.058 1.058 La₂O₃ 1.08 0.486 0.2115 0.6975 Li₂O 0 0 3.33 3.33 MgO 0.42 0.189 0 0.189 MnO 0.9 0.405 0.2565 0.6615 Na₂O 13.16 5.922 0.89 6.812 Nd₂O₃ 0.04 0.018 0.288 0.306 NiO 2.68 1.206 0 1.206 PbO 0.01 0.0045 0.126 0.1305 P₂O₃ 0.83 0.3735 0 0.3735 SiO₂ 1.97 0.8865 34.7453 35.6318 SO₃ 0 0 0.0765 0.0765 ZnO 0.15 0.0675 0 0.0675 ZrO₂ 5.73 2.5785 0.702 3.2805

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the AZ-102 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.2:4.2. Zeolite (a natural silicate) was added as a source of part of the glass-forming components.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results of six tests demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.     -   (c) Viscosity: Ranges from 4.66 Pascal second at 1200° C. to         47.9 Pascal second at 950° C.     -   (d) Specific electrical resistivity: Ranges from 4.92 Ωcm at         1200° C. to 10.7 Ωcm at 950° C.     -   (e) PCT results (g/m²/d): Li—1.4×10⁻³; Na—6.2×0⁻²; B—7.2×10⁻³;         Si—1.2×10⁻².     -   (f) TCLP results (mg/L): Ni—0.01; Cr—0.01; Ba—0.507; Pb—0.05;         Ag—0.05; Cd—0.54.

Example 5

Vitrifying Batch 69 Hanford High-Level Waste (HLW) Simulant with 43 Weight Percent Waste Loading

1. The waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 43 weight percent waste loading.

B C D E A Waste 43% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 18.86 8.1098 3.8902 12 B₂O₃ 0 0 15 15 Bi₂O₃ 4.8 2.064 0 2.064 CaO 4.58 1.9694 1.0306 3 Cr₂O₃ 0.54 0.2322 0 0.2322 F 0.76 0.3268 1.6732 2 Fe₂O₃ 10.48 4.5064 5.4936 10 K₂O 0.12 0.0516 0.9484 1 Li₂O 0 0 4 4 MnO 1.08 0.4644 0 0.4644 Na₂O 23.36 10.0448 0 10.0448 NiO 0.96 0.4128 0 0.4128 P₂O₅ 2.74 1.1782 0 1.1782 PbO 0.32 0.1376 0 0.1376 SiO₂ 23.26 10.0018 24.9982 35 SO₃ 0.12 0.0516 0 0.0516 SrO 0.79 0.3397 0 0.3397 U₃O₈ 6.86 2.9498 0 2.9498 ZrO 0.11 0.0473 0 0.0473

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 69 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2).

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <0.5 vol % crystals         (spinel) were found.     -   (c) TCLP results (mg/L): Ni —0.12; Cr —0.024; Pb —0.04.

Viscosity, specific electrical resistivity, and PCT were not measured. Due to the similarity of this glass composition to the C-106 composition, the results were expected to be similar.

Example 6

Vitrifying Batch 56 Hanford High-Level Waste (HLW) Simulant with 55 Weight Percent Waste Loading

1. The Batch 56 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 55 weight percent waste loading.

B C D E A Waste 55% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 15.47 8.5085 1.23476 9.74326 B₂O₃ 0.15 0.0825 15.1807 15.2632 BaO 0.65 0.3575 0 0.3575 Bi₂O₃ 9.03 4.9665 0 4.9665 CaO 4.11 2.2605 0 2.2605 CdO 0.06 0.033 0 0.033 Ce₂O₃ 0.05 0.0275 0 0.0275 Cl 0 0 0.1482 0.1482 Cr₂O₃ 1.26 0.693 0 0.693 Cs₂O 0 0 0.0684 0.0684 CuO 0.11 0.0605 0.0003 0.0608 F 1.18 0.649 0.636 1.285 Fe₂O₃ 21.88 12.034 5.539 17.573 K₂O 0.38 0.209 0.6671 0.8761 La₂O₃ 1.03 0.5665 0 0.5665 Li₂O 0 0 1.842 1.842 MgO 1.33 0.7315 1.0825 1.814 MnO 2.76 1.518 3.9578 5.4758 Na₂O 18.57 10.2135 0 10.2135 Nd₂O₃ 0 0 0.2052 0.2052 NiO 1.18 0.649 0 0.649 P₂O₅ 3.85 2.1175 0 2.1175 PbO 0.73 0.4015 0 0.4015 SiO₂ 8.75 4.8125 26.0494 30.8619 SrO 0.16 0.088 1.1698 1.2578 ThO₂ 0.05 0.0275 0 0.0275 TiO₂ 0 0 0.1938 0.1938 U₃O₈ 4.94 2.717 0 2.717 ZnO 0.07 0.0385 0.0565 0.095 ZrO₂ 1.73 0.9515 0 0.9515

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 56 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.14:3.9.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <0.2 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 7

Vitrifying Batch 35 Hanford High-Level Waste (HLW) Simulant with 40 Weight Percent Waste Loading

1. The Batch 35 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 35 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.18:2.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 27.66 11.064 0 11.064 B₂O₃ 0.71 0.284 14.976 15.26 Bi₂O₃ 0.23 0.092 0 0.092 CaO 1.49 0.596 0.434 1.03 Cr₂O₃ 2.42 0.968 0 0.968 F 2.13 0.852 0.428 1.28 Fe₂O₃ 5.66 2.264 7.736 10 K₂O 1.23 0.492 0.378 0.87 Li₂O 0.22 0.088 1.752 1.84 MgO 0.06 0.024 1.786 1.81 MnO 1.29 0.516 4.954 5.47 Na₂O 24.87 9.948 0 9.948 NiO 0.91 0.364 0 0.364 P₂O₅ 1.48 0.592 0 0.592 PbO 0.4 0.16 0.03 0.19 SiO₂ 6.82 2.728 28.132 30.86 SrO 0.19 0.076 1.184 1.26 ThO₂ 0.37 0.148 0 0.148 U₃O₈ 10.07 4.028 0 4.028 ZrO₂ 11.25 4.5 0 4.5

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: <0.3 vol % (spinel)         crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: 2 vol % crystals         (spinel) were found. Average size <10 microns.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 8

Vitrifying Batch 46 Hanford High-Level Waste (HLW) Simulant with 45 Weight Percent Waste Loading

1. The Batch 46 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 45 weight percent waste loading.

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 46 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.11:2.

B C D E A Waste 45% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 18.11 8.1495 6.2505 14.4 B₂O₃ 0.28 0.126 14.874 15 Bi₂O₃ 2.09 0.9405 0 0.9405 CaO 5.07 2.2815 0.0005 2.282 Cr₂O₃ 1.29 0.5805 0 0.5805 F 3.08 1.386 0 1.386 Fe₂O₃ 12.27 5.5215 0 5.5215 K₂O 0.35 0.1575 0 0.1575 Li₂O 0.03 0.0135 1.8265 1.84 MgO 0.28 0.126 0 0.126 MnO 1.95 0.8775 0 0.8775 Na₂O 24.16 10.872 0 10.872 NiO 3.1 1.395 0 1.395 P₂O₅ 5.02 2.259 0 2.259 PbO 0.62 0.279 0 0.279 SiO₂ 5.92 2.664 32.336 35 SrO 1.87 0.8415 0 0.8415 ThO₂ 0.3 0.135 0 0.135 U₃O₈ 12.03 5.4135 0 5.4135 ZrO₂ 0.93 0.4185 0 0.4185

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: 0.2 vol % (spinel)         crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 9

Vitrifying Batch 53 Hanford High-Level Waste (HLW) Simulant with 50 Weight Percent Waste Loading

1. The Batch 53 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 50 weight percent waste loading.

B C D E A Waste 50% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 16.42 8.21 1.53 9.74 B₂O₃ 0.07 0.035 13.965 14 Bi₂O₃ 10.63 5.315 0 5.315 CaO 3.62 1.81 0 1.81 Cr₂O₃ 0.73 0.365 0 0.365 F 5.09 2.545 0 2.545 Fe₂O₃ 14.99 7.495 2.505 10 K₂O 0.15 0.075 0.795 0.87 Li₂O 0.01 0.005 1.835 1.84 MgO 0.11 0.055 1.745 1.8 MnO 0.58 0.29 1.58 1.87 Na₂O 19.93 9.965 0 9.965 NiO 1.01 0.505 0 0.505 P₂O₅ 4.77 2.385 0 2.385 PbO 0.66 0.33 0 0.33 SiO₂ 9.18 4.59 26.27 30.86 SrO 0.52 0.26 0 0.26 ThO₂ 0.06 0.03 0 0.03 U₃O₈ 10.88 5.44 0 5.44 ZrO₂ 0.18 0.09 0.01 0.1

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 53 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1.1:1:2.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <0.5 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 10

Vitrifying Batch 62 Hanford High-Level Waste (HLW) Simulant with 40 Weight Percent Waste Loading

1. The Batch 62 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 14.84 5.936 3.804 9.74 B₂O₃ 0.34 0.136 14.864 15 Bi₂O₃ 0.02 0.008 0 0.008 CaO 0.86 0.344 0.686 1.03 CdO 2.91 1.164 0 1.164 Cr₂O₃ 0.06 0.024 0 0.024 F 0.56 0.224 1.056 1.28 Fe₂O₃ 42.85 17.14 0 17.14 K₂O 0.98 0.392 0.478 0.87 La₂O₃ 1.56 0.624 0 0.624 Li₂O 0.05 0.02 1.82 1.84 MgO 0.4 0.16 0 0.16 MnO 0.52 0.208 0 0.208 Na₂O 11.45 4.58 5 9.58 NiO 2.35 0.94 0 0.94 P₂O₅ 0.03 0.012 0 0.012 PbO 0.13 0.052 0 0.052 SiO₂ 0.21 0.084 33.252 33.336 SrO 0.12 0.048 0 0.048 ThO₂ 0.23 0.092 0 0.092 U₃O₈ 2.61 1.044 0 1.044 ZrO₂ 14.52 5.808 0 5.808

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 62 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.38:2.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 11

Vitrifying Batch 87 Hanford High-Level Waste (HLW) Simulant with 50 Weight Percent Waste Loading

1. The Batch 87 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 50 weight percent waste loading.

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 87 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1.03:1:2.

B C D E A Waste 50% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 25.79 12.895 0 12.895 B₂O₃ 0.47 0.235 14.765 15 Bi₂O₃ 5.31 2.655 0 2.655 CaO 2.34 1.17 0 1.17 Cr₂O₃ 1.67 0.835 0 0.835 F 1.01 0.505 0.775 1.28 Fe₂O₃ 11.84 5.92 0 5.92 K₂O 2.03 1.015 0 1.015 Li₂O 0.04 0.02 3.74 3.76 MgO 0.56 0.28 0 0.28 MnO 2.56 1.28 0 1.28 Na₂O 22.9 11.45 0 11.45 NiO 2.25 1.125 0 1.125 P₂O₅ 3.76 1.88 0 1.88 PbO 0.49 0.245 0 0.245 SiO₂ 5.16 2.58 32.42 35 SrO 0.22 0.11 0 0.11 ThO₂ 0.39 0.195 0 0.195 U₃O₈ 6.62 3.31 0 3.31 ZrO₂ 1.23 0.615 0 0.615

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: 0.3 vol % (spinel)         crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <0.5 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 12

Vitrifying Batch 34 Hanford High-Level Waste (HLW) Simulant with 50 Weight Percent Waste Loading

1. The Batch 34 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 50 weight percent waste loading.

B C D E A Waste 50% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 21.78 10.89 0 10.89 B₂O₃ 0.44 0.22 14.78 15 Bi₂O₃ 0.24 0.12 0 0.12 CaO 1.87 0.935 0 0.935 Cr₂O₃ 2.11 1.055 0 1.055 F 1.43 0.715 0.54 1.255 Fe₂O₃ 6.43 3.215 5.785 9 K₂O 0.66 0.33 0.54 0.87 Li₂O 0.14 0.07 1.77 1.84 MgO 0.04 0.02 1.79 1.81 MnO 1.03 0.515 4.485 5 Na₂O 22.77 11.385 0 11.385 NiO 0.65 0.325 0 0.325 P₂O₅ 1.83 0.915 0 0.915 PbO 0.42 0.21 0 0.21 SiO₂ 20.95 10.475 20.525 31 SrO 0.15 0.075 0 0.075 ThO₂ 0.33 0.165 0 0.165 U₃O₈ 11.11 5.555 0 5.555 ZrO₂ 5.19 2.595 0 2.595

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 34 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1.1:1:2.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <0.1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 13

Vitrifying Batch 32 Hanford High-Level Waste (HLW) Simulant with 50 Weight Percent Waste Loading

1. The Batch 32 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 50 weight percent waste loading.

B C D E A Waste 50% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 12.98 6.49 3.21 9.7 B₂O₃ 0.05 0.025 14.975 15 Bi₂O₃ 0.28 0.14 0 0.14 CaO 2.31 1.155 0 1.155 Cr₂O₃ 1.37 0.685 0 0.685 F 0.78 0.39 0.91 1.3 Fe₂O₃ 6.66 3.33 9.34 12.67 K₂O 0.3 0.15 0.72 0.87 Li₂O 0 0 1.9 1.9 MgO 0.02 0.01 1.8 1.81 MnO 0.72 0.36 4.84 5.2 Na₂O 21.44 10.72 0 10.72 NiO 0.2 0.1 0 0.1 P₂O₅ 1.9 0.95 0 0.95 PbO 0.37 0.185 0.005 0.19 SiO₂ 36.22 18.11 12.75 30.86 SrO 0.19 0.095 0.005 0.1 ThO₂ 0.26 0.13 0 0.13 U₃O₈ 12.3 6.15 0 6.15 ZrO₂ 0.37 0.185 0.185 0.37

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 32 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.16:2.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results of six tests demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 14

Vitrifying Batch 20 Hanford High-Level Waste (HLW) Simulant with 40 Weight Percent Waste Loading

1. The Batch 20 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 20 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO): R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.19:2.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 6.8 2.72 7.023 9.743 B₂O₃ 0.62 0.248 15.015 15.263 BaO 0.25 0.1 0 0.1 Bi₂O₃ 3.82 1.528 0 1.528 CaO 0.71 0.284 0.747 1.031 Ce₂O₃ 0.37 0.148 0 0.148 Cl 0.148 0.0592 0.0888 0.148 Cr₂O₃ 0.18 0.072 0.034 0.106 Cs₂O 0.068 0.0272 0.0408 0.068 CuO 0.061 0.0244 0.0366 0.061 F 2.37 0.948 0.337 1.285 Fe₂O₃ 14.4 5.76 11.813 17.573 K₂O 0.46 0.184 0.692 0.876 La₂O₃ 0.2 0.08 0.251 0.331 MgO 0.55 0.22 1.594 1.814 MnO 6.35 2.54 2.9358 5.4758 Na₂O 12.65 5.06 4.524 9.584 Nd₂O₃ 0.32 0.128 0.077 0.205 NiO 0.45 0.18 0.055 0.235 P₂O₅ 0.74 0.296 0 0.296 PbO 0.76 0.304 0 0.304 SiO₂ 4.67 1.868 28.994 30.862 SrO 12.66 5.064 0 5.064 TiO₂ 0.194 0.0776 0.1164 0.194 U₃O₈ 6.18 2.472 0 2.472 ZrO₂ 22.96 9.184 0 9.184 Li₂O 1.842 0.7368 1.1052 1.842 ZnO 0.095 0.038 0.057 0.095

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: <0.3 vol % (spinel)         crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <2 vol % crystals         (spinel) were found. Average size <10 microns.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 15

Vitrifying Batch 4 Hanford High-Level Waste (HLW) Simulant with 40 Weight Percent Waste Loading

1. The Batch 4 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 4 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.28:2.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 7.05 2.82 7.18 10 B₂O₃ 0.33 0.132 14.868 15 Bi₂O₃ 0.01 0.004 0 0.004 CaO 2.93 1.172 0 1.172 Cr₂O₃ 0.19 0.076 0 0.076 F 0.04 0.016 1.264 1.28 Fe₂O₃ 46.2 18.48 0 18.48 K₂O 0.15 0.06 0.81 0.87 Li₂O 0 0 1.84 1.84 MgO 2.01 0.804 0 0.804 MnO 8.9 3.56 0 3.56 Na₂O 14.09 5.636 3.944 9.58 NiO 1.45 0.58 0 0.58 P₂O₅ 0.61 0.244 0 0.244 PbO 1.45 0.58 0 0.58 SiO₂ 5.26 2.104 30.896 33 SrO 0.16 0.064 1.196 1.26 ThO₂ 0 0 0 0 U₃O₈ 1.44 0.576 0 0.576 ZrO₂ 0.62 0.248 0 0.248

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 16

Vitrifying Batch 30 Hanford High-Level Waste (HLW) Simulant with 40 Weight Percent Waste Loading

1. The Batch 30 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 15.65 6.26 7.74 14 B₂O₃ 0.49 0.196 14.804 15 Bi₂O₃ 0.11 0.044 0 0.044 CaO 0.59 0.236 0 0.236 Cr₂O₃ 5.41 2.164 0 2.164 F 0.86 0.344 0.936 1.28 Fe₂O₃ 6.66 2.664 6.736 9.4 K₂O 2.37 0.948 0 0.948 Li₂O 0.05 0.02 0 0.02 MgO 0.4 0.16 0 0.16 MnO 1.44 0.576 0 0.576 Na₂O 49.3 19.72 0 19.72 NiO 0.35 0.14 0 0.14 P₂O₅ 2.74 1.096 0 1.096 PbO 0.36 0.144 0 0.144 SiO₂ 0.47 0.188 30.812 31 SrO 0.03 0.012 0 0.012 ThO₂ 0.22 0.088 0 0.088 U₃O₈ 3.93 1.572 0.007 1.579 ZrO₂ 5.99 2.396 0 2.396

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 30 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.06:2.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

Example 17

Vitrifying Savannah River Sludge Batch 2 High-Level Waste (HLW) Simulant With 40 Weight Percent Waste Loading

1. The Savannah River Sludge Batch 2 waste composition from Column A was used according to the amounts in Column B. Column C shows the amount (in weight percent) of the components found in the final glass product with a 40 weight percent waste loading.

B C D E A Waste 40% Waste Additives Final Glass Oxides (wt %) (wt %) (wt %) (wt %) Al₂O₃ 17.03 6.812 1.188 8 B₂O₃ 0 0 14 14 BaO 0.27 0.108 0 0.108 CaO 3.81 1.524 0 1.524 Cr2O3 0.37 0.148 0 0.148 Cu₂O 0.2 0.08 0 0.08 F 0 0 2.4 2.4 Fe₂O₃ 42.76 17.104 0 17.104 K₂O 0.08 0.032 0 0.032 Li₂O 0 0 3 3 MgO 0.23 0.092 0 0.092 MnO2 4.82 1.928 0 1.928 Na₂O 12.23 4.892 7.608 12.5 NiO 2.2 0.88 0 0.88 PbO 0.33 0.132 0 0.132 SiO₂ 2 0.8 31.8 32.6 SrO 0.1 0.04 0 0.04 U₃O₈ 12.37 4.948 0 4.948 ZnO 0.39 0.156 0 0.156 ZrO₂ 0.79 0.316 0 0.316

2. Glass-forming components according to the amounts in Column D were added to the waste composition, producing the final glass composition shown in Column E. The exact amounts of glass-forming components used were calculated together with the Batch 2 waste components, so that the total amount of the components would achieve a molar ratio of (R₂O+RO):R₂O₃:(RO₂+R₂O₅) within the range of about (1-1.3):(1-1.4):(1.2-4.2). The molar ratio achieved was approximately 1:1.22:1.7.

3. The mixture of step 1 and step 2 were stirred together for 1 hour at ambient temperature, producing an aqueous suspension.

4. The product of step 3 was then melted at 1150° C. for 5 hours in a muffle furnace, and then quenched.

5. The resultant glass was then tested to determine the suitability of this composition for processing using liquid-fed ceramic melter (LFCM) technology. The results demonstrated that the composition was suitable for processing using LFCM technology:

-   -   (a) Crystallinity after being quenched: No crystals were found.     -   (b) Crystallinity after 3 days at 950° C.: <1 vol % crystals         (spinel) were found.

Viscosity, specific electrical resistivity, PCT and TCLP were not verified. Due to the similarity of the major glass components of this glass to those of C-106, the results were expected to be similar.

The foregoing disclosure of the preferred embodiments of the present invention has been presented for purposes of illustration and description. It is not intended to be exhaustive or to limit the invention to the precise forms disclosed. Many variations and modifications of the embodiments described herein will be apparent to one of ordinary skill in the art in light of the above disclosure. The scope of the invention is to be defined only by the claims appended hereto, and by their equivalents.

Further, in describing representative embodiments of the present invention, the specification may have presented the method and/or process of the present invention as a particular sequence of steps. However, to the extent that the method or process does not rely on the particular order of steps set forth herein, the method or process should not be limited to the particular sequence of steps described. As one of ordinary skill in the art would appreciate, other sequences of steps may be possible. Therefore, the particular order of the steps set forth in the specification should not be construed as limitations on the claims. In addition, the claims directed to the method and/or process of the present invention should not be limited to the performance of their steps in the order written, and one skilled in the art can readily appreciate that the sequences may be varied and still remain within the spirit and scope of the present invention. 

1-11. (canceled)
 12. A borosilicate glass consisting essentially of: about 1 to about 1.3 mole parts of a combination of monovalent cation oxides (R₂O) and divalent cation oxides (RO); about 1 to about 1.4 mole parts trivalent cation oxides (R₂O₃); about 1.2 to about 4.2 mole parts of a combination of tetravalent cation oxides (RO₂) and pentavalent cation oxides (R₂O₅); and wherein SiO₂ is present in an amount greater than 30 weight percent, B₂O₃ is present in an amount between 8.7 and 15.3 weight percent, Al₂O₃ is present in an amount between 7 and 15.1 weight percent, CaO is present in an amount between 0.2 and 2.3 weight percent, and fluorine is present in an amount between about 1 to about 3 weight percent.
 13. The borosilicate glass, according to claim 12, consisting essentially of: about 1 to about 1.3 mole parts of a combination of monovalent cation oxides (R₂O) and divalent cation oxides (RO), including alkaline oxides and alkaline earth oxides; about 1 to about 1.4 mole parts trivalent cation oxides (R₂O₃), including alumina, boric oxide, and ferric oxide; about 1.2 to about 4.2 mole parts of a combination of tetravalent cation oxides (RO₂) and pentavalent cation oxides (R₂O₅), including silica, zirconia, titania, and phosphoric oxide; and about 1 to about 3 weight percent fluorine; wherein SiO₂ is present in an amount greater than 30 weight percent, B₂O₃ is present in an amount between 8.7 and 15.3 weight percent, Al₂O₃ is present in an amount between 7 and 15.1 weight percent, and CaO is present in an amount between 0.2 and 2.3 weight percent.
 14. The borosilicate glass of claim 12, wherein the borosilicate glass is peraluminous.
 15. The borosilicate glass of claim 12, wherein the borosilicate glass has a viscosity of 2 to 10 Pascal second at a temperature of about 1150 to about 1200 degrees Celsius.
 16. The borosilicate glass of claim 12, wherein the borosilicate glass has a calculated degree of polymerization (K) less than about
 15. 17. The borosilicate glass of claim 12, wherein the borosilicate glass has a calculated degree of polymerization (K) less than about
 7. 18. The borosilicate glass of claim 12, wherein the borosilicate glass has crystallinity of less than 1 volume percent at about 1150 degrees Celsius, and crystallinity of up to 2 volume percent after three days at about 950 degrees Celsius.
 19. The borosilicate glass of claim 12, wherein the borosilicate glass has specific electrical resistivity ranging between about 1.40 cm to about 10 Ωcm at about 1150 degrees Celsius, that is acceptable for processing in vitrification melters.
 20. The borosilicate glass of claim 12, wherein the borosilicate glass meets the leaching requirements of less than about 1.19 grams per square meter per day for boron, less than about 0.69 grams per square meter per day for lithium, and less than about 0.95 grams per square meter per day for sodium, for acceptance in U.S. high-level waste repositories.
 21. The borosilicate glass of claim 12, wherein the borosilicate glass contains fluorine in an amount between about 1.2 and about 2.5 weight percent. 